Low temperature process for fabricating layered superlattice materials and making electronic devices including same

ABSTRACT

A coating of liquid precursor containing a metal is applied to a first electrode, baked on a hot plate in oxygen ambient at a temperature not exceeding 300° C. for five minutes, then RTP annealed at 675° C. for 30 seconds. The coating is then annealed in oxygen or nitrogen ambient at 700° C. for one hour to form a thin film of layered superlattice material with a thickness not exceeding 100 nm. A second electrode is applied to form a capacitor, and a second anneal is performed in oxygen or nitrogen ambient at a temperature not exceeding 700° C. If the material is strontium bismuth tantalate, the precursor contains u mole-equivalents of strontium, v mole-equivalents of bismuth, and w mole-equivalents of tantalum, where 0.8≦u≦1.0, 2.0≦v≦2.3, and 1.9≦w≦2.1.

BACKGROUND OF THE INVENTION

1. Field of the Invention

The invention in general relates to the fabrication of layered superlattice materials, and more particularly to fabrication processes that provide high-polarizability and low fatigue ferroelectric integrated circuit devices and low-leakage current high dielectric constant integrated circuit devices using low processing temperatures.

2. Statement of the Problem

Ferroelectric compounds possess favorable characteristics for use in nonvolatile integrated circuit memories. See Miller, U.S. Pat. No. 5,046,043. A ferroelectric device, such as a capacitor, is useful as a nonvolatile memory when it possesses desired electronic characteristics, such as high residual polarization, good coercive field, high fatigue resistance, and low leakage current. Layered superlattice material oxides have been studied for use in integrated circuits. U.S. Pat. No. 5,434,102, issued Jul. 18, 1995, to Watanabe et. al., and U.S. Pat. No. 5,468,684, issued Nov. 21, 1995, to Yoshimori et al., describe processes for integrating these materials into practical integrated circuits. Layered superlattice materials exhibit characteristics in ferroelectric memories that are orders of magnitude superior to alternative types of ferroelectric materials, such as PZT and PLZT compounds.

Integrated circuit devices containing ferroelectric elements with layered superlattice materials are currently being manufactured. The layered superlattice materials comprise metal oxides. The presence of oxides causes problems because the oxygen diffuses through the various materials contained in the integrated circuit and combines with atoms in the substrate and in semiconductor layers forming oxides. The resulting oxides interfere with the function of the integrated circuit; for example, they may act as dielectrics in the semiconducting regions, there by virtually forming capacitors. Diffusion of atoms from the underlying substrate and other circuit layers into the ferroelectric metal oxide is also a problem; for example, silicon from a silicon substrate and from polycrystalline silicon contact layers is known to diffuse into layered superlattice material and degrade its ferroelectric properties. For relatively low-density applications, the ferroelectric memory capacitor is placed on the side of the underlying CMOS circuit, and this may reduce somewhat the problem of undesirable diffusion of atoms between circuit elements. Nevertheless, as the market demand and the technological ability to manufacture high-density circuits increase, the distance between circuit elements decreases, and the problem of molecular and atomic diffusion between elements becomes more acute. To achieve high circuit density by reducing circuit area, the ferroelectric capacitor of a memory cell is placed virtually on top of the switch element, typically a field-effect transistor (hereinafter “FET”), and the switch and bottom electrode of the capacitor are electrically connected by a conductive plug. To inhibit undesired diffusion, a barrier layer is located under the ferroelectric oxide, between the capacitor's bottom electrode and the underlying layers. The barrier layer not only must inhibit the diffusion of oxygen and other chemical species that may cause problems; it must also be electrically conductive, to enable electrical connection between the capacitor and the switch. The maximum processing temperature allowable with current barrier technology is about 700° C. At temperatures above 700° C., the highest-temperature barrier materials degrade and lose their diffusion-barrier properties. On the other hand, the minimum feasible manufacturing process temperatures of layered superlattice materials used in the prior art is about 800° C., which is the temperature at which deposited layered superlattice materials are annealed to achieve good crystallization. Good ferroelectric properties have been achieved in the prior art using process heating temperatures at about 700° C. See U.S. Pat. No. 5,508,226, issued Apr. 16, 1996, to Ito et. al. Nevertheless, the annealing and other heating times in the low-temperature methods disclosed in the prior art are in the range of three to six hours, which is economically unfeasible.

For the above reasons, therefore, it would be useful to have a low-temperature method for fabricating layered superlattice materials in ferroelectric integrated circuits in which the heating time was much less than three to six hours.

SUMMARY OF THE INVENTION

The present invention provides a fabrication method that utilizes only temperatures not exceeding 700° C. with total heating times of less than two hours to fabricate high quality layered integrated circuit devices utilizing layered superlattice materials.

The invention provides a method of fabricating a thin film of layered superlattice material comprising: providing a substrate and a precursor containing metal moieties in effective amounts for spontaneously forming a layered superlattice material upon heating the precursor; applying the precursor to the substrate to form a coating; and heating the coating at a temperature not exceeding 700° C. for a total time not exceeding two hours to form the thin film of layered superlattice material on the substrate.

In one aspect of the invention, the heating includes a step of baking the coating on the substrate at a temperature not exceeding 300° C. Another feature is that the step of baking is conducted for a time period not exceeding 15 minutes in an oxygen-enriched ambient. Typically, the oxygen-enriched ambient is substantially pure oxygen gas (hereinafter “O₂ gas”).

A feature of the invention is that heating comprises a step of rapid thermal processing the coating. The step of rapid thermal processing is conducted at a temperature not exceeding 700° C. In a preferred embodiment, the rapid thermal processing is conducted for 30 seconds with a ramping rate of 100° C. per second.

An important feature of the invention is that heating comprises a step of annealing the coating at a temperature not exceeding 700° C., preferably for a time period not exceeding one and one-half hours. In one embodiment of the invention, the annealing is conducted in an oxygen-enriched ambient, typically in O₂ gas. In another embodiment of the invention, the annealing is conducted in oxygen-deficient ambient, typically substantially pure nitrogen gas (hereinafter “N₂ gas”).

In one aspect of the invention, the substrate comprises a first electrode, and the method includes steps of forming a second electrode on the coating, after the step of annealing, to form a capacitor, and subsequently performing a step of post-annealing. In a preferred embodiment, the first electrode and the second electrode contain platinum and titanium. The step of post-annealing is conducted at a temperature not exceeding 700° C., preferably for a time period not exceeding 30 minutes. In one embodiment of the invention, the post-annealing is conducted in an oxygen-enriched ambient, typically in O₂ gas. In another embodiment of the invention, the post-annealing is conducted in oxygen-deficient ambient, typically N₂ gas.

In a preferred embodiment of the invention, an electrically conductive barrier layer is formed on the substrate prior to applying the precursor coating.

In a preferred embodiment of the inventive method, the heating comprises steps of baking the coating, rapid thermal processing the coating, annealing the coating, and post-annealing the coating. It is a feature of the invention that the total amount of time during which all of these heating steps are conducted does not exceed two hours.

In one embodiment, the thin film of layered superlattice material has a thickness not exceeding 90 nanometers (hereinafter “nm”). In another embodiment, the thin film has a thickness not exceeding 50 nm. In one embodiment, the layered superlattice material comprises strontium bismuth tantalate. Preferably, the corresponding precursor includes u mole-equivalents of strontium, v mole-equivalents of bismuth, and w mole-equivalents of tantalum, and 0.8≦u≦1.0, 2.0≦v≦2.3, and 1.9≦w≦2.1. Ferroelectric capacitors, made according to the method of the invention using experimental precursor solutions in which u=0.9 and v=2.18, show good properties when the ferroelectric thin film has a thickness of either about 50 nm or 100 nm. In another embodiment, the layered superlattice material comprises strontium bismuth tantalum niobate. Preferably, the corresponding precursor includes u mole-equivalents of strontium, v mole-equivalents of bismuth, w mole-equivalents of tantalum, and x equivalents of niobium, and 0.8≦u≦1.0, 2.0≦v≦2.3, 1.9≦w≦2.1, 1.9≦x≦2.1 and 1.9≦(w+x)≦2.1. Preferably, u=0.9 and v=2.18.

An important feature of the invention is baking the coating on the substrate at a temperature not exceeding 300° C. in an oxygen-enriched ambient, typically in O₂ gas.

Numerous other features, objects and advantages of the invention will become apparent from the following description when read in conjunction with the accompanying drawings.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a schematic of a cross-sectional view of a portion of an integrated circuit as may be fabricated by the method of the invention showing a nonvolatile ferroelectric memory cell in which the capacitor is located above the switch;

FIG. 2 is a flow chart showing the preferred embodiment of a process for fabricating a nonvolatile ferroelectric memory device according to the invention;

FIG. 3 is a top view of an exemplary wafer on which thin film capacitors fabricated in accordance with the invention are shown greatly enlarged;

FIG. 4 is a portion of a cross-section of FIG. 3 taken through the lines 4—4, illustrating a thin film capacitor device fabricated in accordance with the invention;

FIG. 5 shows the hysteresis curve of a representative sample capacitor measured at 1.2 volts, plotted on a graph of the polarization value, in units of μC/cm², as a function of applied field, in units of kV/cm;

FIG. 6 is a graph of leakage current, in units A/cm², plotted as a function of applied voltage, measured in the sample capacitor of FIG. 5;

FIG. 7 is a graph of the polarization, in units of μC/cm², plotted as a function of applied field, kV/cm, before fatigue cycling and after 10¹⁰ square-wave cycles in a field of 280 kV/cm, measured in the capacitor of FIGS. 5 and 6;

FIG. 8 shows the hysteresis curve of a representative sample capacitor measured at one volt, plotted as a graph of the polarization value, in units of μC/cm², as a function of applied field, in units of kV/cm;

FIG. 9 shows the hysteresis curve of the capacitor measured at 3 volts, plotted as a graph of the polarization value, in units of μC/cm², as a function of applied field, in units of kV/cm;

FIG. 10 is a graph of leakage current, in units A/cm², plotted as a function of applied voltage;

FIG. 11 is a graph of the polarization, in units of μC/cm², plotted as a function of applied field, kV/cm, before fatigue cycling and after 10¹⁰ square-wave cycles in a field of 280 kV/cm.

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENT

1. Overview

It should be understood that the FIGS. 1, 3 and 4, depicting integrated circuit devices, are not meant to be actual plan or cross-sectional views of any particular portion of an actual integrated circuit device. In the actual devices, the layers will not be as regular and the thicknesses may have different proportions. The various layers in actual devices often are curved and possess overlapping edges. The figures instead show idealized representations which are employed to explain more clearly an fully the method of the invention than would otherwise be possible. Also, the figures represent only one of innumerable variations of ferroelectric devices that could be fabricated using the method of the invention. FIG. 1 depicts a ferroelectric memory containing a switch in the form of a field effect transistor in electrical connection with a ferroelectric capacitor. But the method of this invention can also be used in a ferroelectric FET memory in which the ferroelectric element is incorporated in the switch element. Such a ferroelectric FET was described in McMillan, U.S. Pat. No. 5,523,964. Likewise, other integrated circuits fabricated using the method of the invention could include other elements and compositions of material.

FIG. 1 shows a cross-sectional view of an exemplary nonvolatile ferroelectric memory 100 fabricated according to the invention. The general manufacturing steps for fabricating integrated circuits containing MOSFETs and ferroelectric capacitor elements are described in Mihara, U.S. Pat. No. 5,466,629, and Yoshimori, U.S. Pat. No. 5,468,684, which are hereby incorporated by reference as if fully disclosed herein. General fabrication methods have been described in other references also. Therefore, the elements of the circuit of FIG. 1 will be simply identified here.

In FIG. 1, a field oxide region 104 is formed on a surface of a silicon substrate 102. A source region 106 and a drain region 108 are formed separately from each other within silicon substrate 102. A gate insulating layer 110 is formed on the silicon substrate 104 between the source and drain regions 106 and 108. Further, a gate electrode 112 is formed on the gate insulating layer 110. These source region 106, drain region 108, gate insulating layer 110 and gate electrode 112 together form a MOSFET 114.

A first interlayer dielectric layer (ILD) 116 made of BPSG (boron-doped phospho-silicate glass) is formed on substrate 104 and field oxide region 102. ILD 116 is patterned to form vias 117, 118 to source region 106 and drain region 108, respectively. Vias 117, 118 are filled to form plugs 119, 120, respectively. Plugs 119, 120 are electrically conductive and typically comprise polycrystalline silicon. A diffusion barrier layer 121 is formed and patterned on ILD 116 to be in electrical contact with plug 120. The diffusion barrier layer 121 is made of, for example, titanium nitride, and typically has a thickness of 10-20 nm. Diffusion barrier layers, such as titanium nitride, inhibit the diffusion of chemical species between the underlying and overlying layers of the memory 100.

As depicted in FIG. 1, a bottom electrode layer 122 made of platinum and having a thickness of 100 nm is deposited on diffusion barrier layer 121. Then a ferroelectric thin film 124 is formed on bottom electrode layer 122. A top electrode layer 126, made of platinum and having a thickness of 100 nm, is formed on the ferroelectric thin film 124. Bottom electrode layer 122, ferroelectric thin film 124 and top electrode layer 126 together form ferroelectric capacitor 128. The composition of the ferroelectric thin film 124 is discussed in more detail below.

Wafer substrate 102 may comprise silicon, gallium arsenide or other semiconductor, or an insulator, such as silicon dioxide, glass or magnesium oxide (MgO). The bottom and top electrodes of ferroelectric capacitors conventionally contain platinum. It is preferable that the bottom electrode contains a non-oxidized precious metal such as platinum, palladium, silver, and gold. In addition to the precious metal, metal such as aluminum, aluminum alloy, aluminum silicon, aluminum nickel, nickel alloy, copper alloy, and aluminum copper may be used for electrodes of a ferroelectric memory. Adhesive layers (not shown), such as titanium, enhance the adhesion of the electrodes to adjacent underlying or overlying layers of the circuits.

A second interlayer dielectric layer (ILD) 136 made of NSG (nondoped silicate glass) is deposited to cover ILD 116, diffusion barrier layer 121, and ferroelectric capacitor 128. A PSG (phospho-silicate glass) film or a BPSG (boron phospho-silicate glass) film could also be used in layer 136.

ILD 136 is patterned to form a via 137 to plug 119. A metallized wiring film is deposited to cover ILD 136 and fill via 137 and then patterned to form plug 137, source electrode wiring 138 and top electrode wiring 139. Wirings 138, 139 preferably comprise Al—Si—Cu standard interconnect metal with a thickness of about 200-300 nm.

FIG. 1 depicts only one of many variations of nonvolatile ferroelectric memory cells that can be fabricated using the method of the invention. For example, although the ferroelectric element depicted in FIG. 1 is substantially above the switch element, the invention may be used to fabricate a thin film of layered superlattice material in an element displaced to the side of the switch. Also, the low-temperature method of the invention may be applied to fabricate ferroelectric memory capacitors in which the electrically conductive diffusion barrier layer functions both as a diffusion barrier and as an electrode of the capacitor. Or the low-temperature method of the invention may be used to fabricate circuits that contain no oxygen barrier layer under the ferroelectric thin film.

U.S. Pat. No. 5,519,234 issued May 21, 1996, to Araujo et al., incorporated herein by reference, discloses that layered superlattice compounds, such as strontium bismuth tantalate (SBT), have excellent properties in ferroelectric applications as compared to the best prior art materials and have high dielectric constants and low leakage currents.

The layered superlattice materials may be summarized generally under the formula:

A 1 _(W1) ^(+a1) A 2 _(W2) ^(+a2) . . . Aj _(Wj) ^(+aj) S 1 _(x1) ^(+s1) S 2 _(x2) ^(+s2) . . . Sk _(sk) ^(+sk) B 1 _(y1) ^(+b1) B 2 _(y2) ^(+b2) . . . B1 _(yl) ^(+bl) Q _(z) ⁻²,  (1)

where A1, A2 . . . Aj represent A-site elements in the perovskite-like structure, which may be elements such as strontium, calcium, barium, bismuth, lead, and others; S1, S2 . . . Sk represent superlattice generator elements, which usually is bismuth, but can also be materials such as yttrium, scandium, lanthanum, antimony, chromium, thallium, and other elements with a valence of +3; B1, B2 . . . Bl represent B-site elements in the perovskite-like structure, which may be elements such as titanium, tantalum, hafnium, tungsten, niobium, zirconium, and other elements; and Q represents an anion, which generally is oxygen but may also be other elements, such as fluorine, chlorine and hybrids of these elements, such as the oxyfluorides, the oxychlorides, etc. The superscripts in formula (1) indicate the valences of the respective elements, and the subscripts indicate the number of moles of the material in a mole of the compound, or in terms of the unit cell, the number of atoms of the element, on the average, in the unit cell. The subscripts can be integer or fractional. That is, formula (1) includes the cases where the unit cell may vary throughout the material, e.g. in SrBi₂(Ta_(0.75)N_(0.25))₂O₉, on the average, 75% of the B-sites are occupied by a tantalum atom and 25% of the B-sites are occupied by a niobium atom. If there is only one A-site element in the compound, then it is represented by the “A1” element and w2 . . . wj all equal zero. If there is only one B-site element in the compound, then it is represented by the “B1” element, and y2 . . . yl all equal zero, and similarly for the superlattice generator elements. The usual case is that there is one A-site element, one superlattice generator element, and one or two B-site elements, although formula (1) is written in the more general form since the invention is intended to include the cases where either of the sites and the superlattice generator can have multiple elements. The value of z is found from the equation:

(a 1 w 1+a 2 w 2 . . . +ajwj)+(s 1 x 1+s 2 x 2 . . . +skxk)+(b 1 y 1+b 2 y 2 . . . +blyl)=2z. (2)

Formula (1) includes all three of the Smolenskii type compounds discussed in U.S. Pat. No. 5,519,234 issued May 21, 1996, to Araujo et al., which is hereby incorporated by reference as though fully incorporated herein. The layered superlattice materials do not include every material that can be fit into the formula (1), but only those which spontaneously form themselves into crystalline structures with distinct alternating layers.

The word “substrate” can mean the underlying wafer 102 on which the integrated circuit is formed, as well as any object on which a thin film layer is deposited, such as BPSG layer 116. In this disclosure, “substrate” shall mean the object to which the layer of interest is applied; for example, when we are talking about a bottom electrode, such as 122, the substrate includes the layers 121 and 116 on which the electrode 122 is formed.

The term “thin film” is used herein as it is used in the integrated circuit art. Generally, it means a film of less than a micron in thickness. The thin films disclosed herein are in all instances less than 0.5 microns in thickness. Preferably, the ferroelectric thin film 124 is 40 nm to 100 nm thick. These thin films of the integrated circuit art should not be confused with the layered capacitors of the macroscopic capacitor art which are formed by a wholly different process that is incompatible with the integrated circuit art.

The term “stoichiometric” herein may be applied to both a solid film of a material, such as a layered superlattice material, or to the precursor for forming a material. When it is applied to a solid thin film, it refers to a formula which shows the actual relative amounts of each element in a final solid thin film. When applied to a precursor, it indicates the molar proportion of metals in the precursor. A “balanced” stoichiometric formula is one in which there is just enough of each element to form a complete crystal structure of the material with all sites of the crystal lattice occupied, though in actual practice there always will be some defects in the crystal at room temperature. For example, both SrBi₂(TaNb)O₉ and SrBi₂(Ta_(1.5)Nb_(0.5))O₉ are balanced stoichiometric formulae. In contrast, a precursor for strontium bismuth tantalum niobate in which the molar proportions of strontium, bismuth, tantalum, and niobium are 0.9, 2.18, 1.5, and 0.5, respectively, is represented herein by the unbalanced “stoichiometric” formula Sr_(0.9)Bi_(2.18)(Ta_(1.5)Nb_(0.5))O₉, since it contains excess bismuth and deficient strontium relative to the B-site elements tantalum and niobium. In this disclosure, an “excess” amount of a metallic element means an amount greater than required to bond with the other metals present to make a completed crystalline structure of the desired material, with all atomic sites occupied and no amount of any metal left over. A “deficient” amount of a metallic element means an amount less than required to bond with the other metals if the other metals were present in stoichiometrically balanced amounts.

2. Description of Preferred Method

The diagram of FIG. 2 is a flow sheet of the fabrication steps of the process 210 including the method of this invention to make a ferroelectric memory as depicted in FIG. 1. In step 212, a semiconductor substrate is provided on which a switch is formed in step 214. The switch is typically a MOSFET. In step 216, an insulating layer is formed to separate the switching element from the ferroelectric element to be formed. Using conventional processes, the insulating layer is patterned to form vias, which are filled with conductive plugs to electrically connect the switch to the memory capacitor and the rest of the integrated circuit. In step 218, a diffusion barrier layer is deposited on the insulating layer and patterned. Preferably the diffusion barrier comprises titanium nitride and has a thickness of about 10-20 nm. Preferably, the diffusion barrier is deposited by a conventional sputtering method, using a titanium nitride target, although a titanium target with a nitrogen-containing sputter gas may also be used. In step 220, a bottom electrode is formed. Preferably, the electrode is made of platinum and is sputter-deposited to form a layer with a thickness of about 200 nm. The precursor for forming the ferroelectric thin film of layered superlattice material is applied to the bottom electrode in step 224. In the method of the invention, the precursor is applied using a liquid deposition technique, such as a misted deposition method as described in U.S. Pat. No. 5,456,945, or a spin-coating method. In step 222, chemical precursors of the layered superlattice material that will form the desired ferroelectric thin film are prepared. Usually, precursor solutions are prepared from commercially available solutions containing the chemical precursor compounds. But the preferred embodiment of the inventive method utilizes a liquid precursor solution containing relative molar proportions of the elements strontium, bismuth, and tantalum corresponding approximately to the formula Sr_(0.9)Bi_(2.18)Ta₂O₉; therefore, if necessary, the concentrations of the various precursors supplied in the commercial solutions are adjusted in step 222 to accommodate particular manufacturing or operating conditions. According to the invention, a liquid coating of precursor solution is applied to the substrate in step 224. In the examples below, the substrate is spun at 1500-2000 rpm for 30 seconds. In baking step 226, the coating of liquid precursor is baked and dried at a temperature not exceeding 300° C. Preferably, the baking step is conducted on a hot plate in substantially pure O₂ gas, or at least in an oxygen-enriched ambient, for a time period not exceeding 15 minutes. The term “oxygen-enriched” means that the relative amount of oxygen present is in excess of the amount of oxygen present in air.

Then, in step 228, the dried coating on the substrate is subjected to rapid thermal processing (“RTP”). The RTP is conducted at a temperature not exceeding 700° C. Preferably, the RTP is conducted for 30 seconds with a ramping rate of 100° C. per second. Radiation from a halogen lamp, an infrared lamp, or an ultraviolet lamp provides the source of heat for the RTP bake step. In the examples below, an AG Associates model 410 Heat Pulser utilizing a halogen source was used. Preferably, the RTP bake is performed in substantially pure O₂ gas, or at least in an oxygen-enriched ambient. Any residual organics are burned out and vaporized during the RTP process. At the same time, the rapid temperature rise of the RTP bake promotes nucleation; that is, the generation of numerous crystalline grains of the layered superlattice material in the solid film 30. These grains act as nuclei upon which further crystallization can occur. The presence of oxygen in the bake process is essential in forming these grains.

In annealing step 230, the coating is annealed at a temperature not exceeding 700° C. to form the thin film of layered superlattice material. The annealing time does not exceed one and one-half hours. Preferably, the annealing time is about 60 minutes. The anneal is typically performed in a furnace containing an O₂ gas ambient, but good experimental results were also obtained using an oxygen-free N₂ gas ambient. The annealing step can also be conducted in air, in an oxygen-enriched ambient, or in an “oxygen-deficient” ambient in which the relative amount of oxygen is less than the relative amount of oxygen in air. The sequence of steps 224-230 may be conducted a second time (indicated by the dashed flowline in FIG. 2) to achieve the desired quality and thickness of the ferroelectric thin film. Depending on the thickness of the initial coating, the thickness of the thin film after one sequence of steps 224-230 ranges between 40 nm and 100 nm. Preferably, two sequences of steps 224-230, each sequence forming a layer with a thickness of 40-50 nm, are used to form a ferroelectric thin film with a total thickness of 80-100 nm. For process-economical reasons, however, it might be desirable to form a thin film of 80-100 nm thickness using one sequence of steps 224-230. Or, for example, to increase circuit density, it might be preferable to use one sequence of steps 224-230 to form a thin film having a thickness in the range of 40-50 nm.

Following steps 224-230, the top electrode is formed in step 232. Preferably, the electrode is formed by RF sputtering of a platinum single layer, but it also may be formed by DC sputtering, ion beam sputtering, vacuum deposition, or other appropriate deposition process. If desirable for the electronic device design, before the metal deposition, the ferroelectric layered superlattice material may be patterned using conventional photolithography and etching, and the top electrode is then patterned in a second process after deposition. In the examples described below, the top electrode and layered superlattice material are patterned together using conventional photolithography techniques and ion beam milling.

In step 234, post-annealing is performed at a temperature not exceeding 700° C. Preferably, post-annealing step 234 is performed for a time period not exceeding 30 minutes. Post-annealing step 234 may be performed in substantially pure O₂ gas or in substantially pure N₂ gas or in mixtures of the two gases, such as air. As deposited, the adhesion of the top electrode to the thin film of layered superlattice material is usually weak. The adhesion is improved by post-annealing. The post-anneal is preferably performed in an electric furnace at a temperature between 500° C. and the anneal temperature, which does not exceed 700° C. A post-anneal below 500° C. does not improve the adhesion of the electrode, and the resulting capacitor devices would tend to be extremely leaky, and shorted in the worst cases.

The post-anneal releases the internal stress in the top electrode and in the interface between the electrode and the ferroelectric thin film. At the same time, the post-annealing step 234 reconstructs microstructure in the layered superlattice material resulting from the sputtering of the top electrode, and as a result improves the properties of the material. The effect is the same whether the post-anneal is performed before or after the patterning steps mentioned in connection with step 236 below. The effect of oxygen ambient during the post-anneal is not as clear as it is in RTP step 228 and anneal step 230 because the layered superlattice material is covered by the top electrode and not exposed to the ambient atmosphere. With regard to most electrical properties, inert gas, such as helium, argon, and nitrogen, may be used with approximately the same result as with oxygen. Nevertheless, it has been found that an oxygen ambient during the post-anneal improves the crystallographic order at the interface of the top electrode and the ferroelectric thin film, as well as the symmetry of the hysteresis curve.

The circuit is generally completed in step 236, which can include a number of substeps; for example, deposition of an ILD, patterning and milling, and deposition of wiring layers.

An important feature of the invention is that the total time of each complete sequence of the various heating steps 226, 228, 230 and 234 does not exceed two hours.

FIG. 3 is a top view of an exemplary wafer on which thin film capacitors 396, 398 and 400 fabricated on substrate 300 in accordance with the invention are shown greatly enlarged. FIG. 4 is a portion of a cross-section of FIG. 3 taken through the lines 4—4, illustrating a thin film capacitor device fabricated in accordance with the invention. A silicon dioxide layer 404 is formed on a silicon crystal substrate 402. Then bottom electrode 422 made of platinum is sputter-deposited on layer 404. Layer 424 is a ferroelectric thin film, and layer 426 represents the top electrode made of platinum.

In the examples below, the ferroelectric and electronic properties of strontium bismuth tantalate capacitors made according to the invention were studied by measuring hysteresis curves, polarizability, leakage current, saturation voltage, fatigue behavior and percentage imprint.

EXAMPLE 1

The capacitors were fabricated from a strontium bismuth tantalate (SBT) liquid precursor solution commercially available from the Kojundo Chemical Corporation. The solution contained amounts of chemical precursors corresponding to the stoichiometric formula Sr_(0.9)Bi_(2.18)Ta₂O₉. The 0.12 mol/l precursor solution contained: bismuth 2-ethylhexanoate, strontium 2-ethylhexanoate, and tantalum 2-ethylhexanoate. The capacitors were formed using one sequence of precursor application and heating steps, and the ferroelectric thin films had a thickness of about 90 nm.

A series of p-type 100 Si wafer substrates 402 were oxidized to form a layer of silicon dioxide 404. A bottom platinum electrode 422 with a thickness of about 200 nm was sputter-deposited on oxide layer 404. These were annealed 30 minutes in O₂ at 650° C., and dehydrated 30 minutes at 180° C. in low vacuum. A spincoat of the 0.12 molar solution of the SBT-precursor was deposited on the bottom electrode 422 at 1800 rpm for 30 seconds. This was dehydrated by baking on a hot plate in O₂ gas for one minute at 160° C., followed by four minutes at 260° C. The coating was crystallized using rapid-thermal-processing (RTP) at 675° C. for 30 seconds in O₂ gas, with a ramping rate of 100° C. per second. The wafer and deposited coating were annealed for 60 minutes at 700° C. in O₂ gas. These steps formed a ferroelectric thin film 424 having a thickness of about 90 nm. Platinum was sputter-deposited to make a top electrode layer 426 with a thickness of about 200 nm. The platinum and strontium bismuth tantalate layers were milled to form the capacitors, and then ashing was performed, followed by a post-anneal for 30 minutes at 700° C. in O₂ gas. The capacitors had a surface area of 7854 μm².

FIG. 5 shows the hysteresis curve of a representative sample capacitor measured at 1.2 volts, plotted on a graph of the polarization value, in units of μC/cm², as a function of applied field, in units of kV/cm. The hysteresis curve was at the saturation voltage, above which voltage remnant polarization, Pr, does not increases more than about ten percent even as voltage is increased without limit. At the saturation voltage of 1.2 volts, therefore, the 2Pr-value was about 13 μC/cm². When measured at 5 volts, the 2Pr-value was about 15 μC/cm². FIG. 6 is a graph of current density measured in the capacitor, in units A/cm², plotted as a function of applied voltage. FIG. 6 shows that at 3 volts, the leakage current was less than 10⁻⁸ A/cm², and at 5 volts, it was still less than 10⁻⁶ A/cm². FIG. 7 shows the fatigue behavior of the sample capacitor. FIG. 7 is a graph of the polarization, in units of μC/cm², plotted as a function of applied field, kV/cm, before fatigue cycling and after 10¹⁰ square-wave cycles in a field of 280 kV/cm. The before and after curves are indistinguishable, indicating that the fatigue is less than one percent after 10¹⁰ cycles. The percentage imprint after 10⁹ cycles at 85° C. and measured at 85° C. was about 20 percent.

EXAMPLE 2

Strontium bismuth tantalate capacitors were prepared as in Example 1, also using only one spin-coating of precursor and, therefore, only one sequence of spin-coating, baking, RTP and annealing steps. But, in this second example, the final ferroelectric thin film had a measured thickness of only 47.5 nm. Also, the hot-plate bake was performed at 160° C. for one minute, as in Example 1, but then at 260° C. for only two minutes, instead of four minutes. Measurements were performed similar to those conducted with the capacitors of Example 1.

FIG. 8 shows the hysteresis curve of a representative sample capacitor measured at one volt, plotted as a graph of the polarization value, in units of μC/cm², as a function of applied field, in units of kV/cm. At one volt, the 2Pr-value, expressed in units of μC/cm², was about 9 μC/cm². FIG. 9 shows the hysteresis curve of the capacitor measured at 3 volts, plotted as a graph of the polarization value, in units of μC/cm², as a function of applied field, in units of kV/cm. At 3 volts, the 2Pr-value, expressed in units of μC/cm², was about 11 μC/cm ². FIG. 10 is a graph of current density, in units A/cm², plotted as a function of applied voltage. At 3 volts, the leakage current in the capacitorwas about 3×10⁻⁷ A/cm², and at 5 volts, it was about 5×10⁻⁶ A/cm². FIG. 11 shows the fatigue behavior of the sample capacitor. FIG. 11 is a graph of the polarization, in units of μC/cm², plotted as a function of applied field, kV/cm, before fatigue cycling and after 10¹⁰ square-wave cycles in a field of 280 kV/cm. The before and after curves are indistinguishable, indicating that the fatigue is less than one percent after 10¹⁰ cycles.

EXAMPLE 3

Strontium bismuth tantalate capacitors were prepared as in Example 2, except that two spin-coatings were used to form the thin film of layered superlattice material. The sequence of spin-coating, baking, RTP and annealing steps was conducted two times, each sequence depositing a film about 40 nm thick. The final ferroelectric thin film had a thickness of about 85 nm, comparable to the thickness of the thin film in Example 1. In contrast to Examples 1 and 2, the annealing step and the post-annealing step were conducted in N₂ gas (instead Of O₂ gas). Measurements were performed similar to those conducted with the capacitors of Example 1.

The 2Pr-value measured at 5 volts in a sample capacitor was 18 μC/cm². The coercive field, 2Ec, measured at 5 volts was 96 kV/cm. The leakage current measured in a field of 300 kV/cm was 7×10⁹ A/cm². The saturation voltage was about one volt. After 10¹⁰ square-wave cycles with 280 kV/cm field, the measured fatigue was about three percent. The percentage imprint after 10⁹ cycles at 85° C. and measured at 85° C. was about 20 percent.

There has been described a low-temperature method for fabricating ferroelectric integrated circuit devices in which the process heating temperature never exceeds 700° C., and which results in devices with good electronic properties. It should be understood that the particular embodiments shown in the d rawings and described within this specification are for purposes of example and should not be construed to limit the invention which will be described in the claims below. Further, it is evident that those skilled in the art may now make numerous uses and modifications of the specific embodiments described without departing from the inventive concepts. For example, now that a low-temperature method for fabricating thin films of layered superlattice materials has been disclosed as a viable part of the process for fabricating ferroelectric memory devices, this method can be combined with other processes to provide variations on the method described. It is also evident that the steps recited may in some instances be performed in a different order; or equivalent structures and processes may be substituted for the various structures and processes described. Consequently, the invention is to be construed as embracing each and every novel feature and novel combination of features present in and/or possessed by the fabrication processes, electronic devices, and electronic device manufacturing methods described. 

We claim:
 1. A method of fabricating a thin film of layered superlattice material comprising: providing a substrate, and a precursor containing metal moieties in effective amounts for spontaneously forming a layered superlattice material upon heating said precursor; applying said precursor to said substrate to form a coating; and heating said coating at a temperature not exceeding 700° C. for a total time not exceeding two hours to form said thin film of layered superlattice material on said substrate.
 2. A method as in claim 1, wherein said heating comprises a step of baking said coating on said substrate at a temperature not exceeding 300° C.
 3. A method as in claim 2, wherein said step of baking is conducted in an oxygen-enriched ambient.
 4. A method as in claim 3, wherein said step of baking is conducted in O₂ gas.
 5. A method as in claim 3, wherein said step of baking is conducted for a time period not exceeding 15 minutes.
 6. A method as in claim 1, wherein said heating comprises a step of rapid thermal processing said coating.
 7. A method as in claim 6, wherein said step of rapid thermal processing is conducted at a temperature not exceeding 675° C.
 8. A method as in claim 6, wherein said step of rapid thermal processing is conducted for 30 seconds with a ramping rate of 100° C. per second.
 9. A method as in claim 1, wherein said heating comprises a step of annealing said coating at a temperature not exceeding 700° C.
 10. A method as in claim 9, wherein said step of annealing is conducted for a time period not exceeding one and one-half hours.
 11. A method as in claim 9, wherein said step of annealing is conducted in an oxygen-enriched ambient.
 12. A method as in claim 9, wherein said step of annealing is conducted in an oxygen-deficient ambient comprising nitrogen.
 13. A method as in claim 12, wherein said step of annealing is conducted in substantially pure N₂ gas.
 14. A method as in claim 1, wherein said substrate comprises a first electrode, and further comprising steps of forming a second electrode on said coating, after said step of heating, to form a capacitor, and subsequently performing a step of post-annealing.
 15. A method as in claim 14, wherein said first electrode and said second electrode each comprise platinum and titanium.
 16. A method as in claim 14, wherein said step of post-annealing is conducted at a temperature not exceeding 700° C. for a time period not exceeding 30 minutes.
 17. A method as in claim 16, wherein said step of post-annealing is conducted in an oxygen-enriched ambient.
 18. A method as in claim 17, wherein said step of post-annealing is conducted in an oxygen-deficient ambient comprising nitrogen.
 19. A method as in claim 18, wherein said step of post-annealing is conducted in substantially pure N₂ gas.
 20. A method as in claim 1, further comprising forming an electrically conductive barrier layer on said substrate prior to said applying said precursor.
 21. A method as in claim 1, wherein said heating comprises steps of baking said coating, rapid thermal processing said coating, annealing said coating, and post-annealing said coating.
 22. A method as in claim 1, wherein said thin film has a thickness not exceeding 90 nm.
 23. A method as in claim 1, wherein said thin film has a thickness not exceeding 50 nm.
 24. A method as in claim 1, wherein said layered superlattice material comprises strontium bismuth tantalate.
 25. A method as in claim 1, wherein said precursor includes u mole equivalents of strontium, v mole-equivalents of bismuth, and w mole-equivalents of tantalum, and 0.8≦u≦1.0, 2.0≦v≦2.3, and 1.9≦w≦2.1.
 26. A method as in claim 25, wherein u=0.9, v=2.18.
 27. A method as in claim 1, wherein said layered superlattice material comprises strontium bismuth tantalum niobate.
 28. A method as in claim 1, wherein said precursor includes u mole-equivalents of strontium, v mole-equivalents of bismuth, w mole-equivalents of tantalum, and x equivalents of niobium, and 0.8≦u≦1.0, 2.0≦v≦2.3, 1.9≦w≦2.1, 1.9≦x≦2.1 and 1.9≦(w+x)≦2.1.
 29. A method as in claim 28, wherein u=0.9, v=2.18.
 30. A method of fabricating a thin film of layered superlattice material comprising: providing a substrate, and a precursor containing metal moieties in effective amounts for spontaneously forming a layered superlattice material upon heating said precursor; applying said precursor to said substrate to form a coating; and baking said coating on said substrate at a temperature not exceeding 300° C. in an oxygen-enriched ambient.
 31. A method as in claim 30, wherein said oxygen-enriched ambient is substantially pure O₂ gas. 